Magnetic apparatus with perpendicular recording medium and head having multilayered reproducing element using tunneling effect

ABSTRACT

The magnetoresistance effect element is of a multilayered structure having at least magnetic layers and an intermediate layer of an insulating material, a semiconductor or an antiferromagnetic material against the magnetic layers, and the magnetoresistance effect element has terminals formed at least on the opposite magnetic layers, respectively, so that a current flows in the intermediate layer. The film surfaces of all the magnetic layers constituting the magnetoresistance effect element are opposed substantially at right angles to the recording surface of a magnetic recording medium. Therefore, the area of the magnetic layers facing the recording surface of the magnetic recording medium can be extremely reduced, and thus the magnetic field from a very narrow region of the high-density recorded magnetic recording medium can be detected by the current which has a tunneling characteristic and passes through the intermediate layer.

BACKGROUND OF THE INVENTION

This is a continuation application of U.S. Ser. No. 10/270,120, filedOct. 15, 2002 now U.S. Pat. No. 6,687,099; which is a continuationapplication of U.S. Ser. No. 09/931,897, filed Aug. 20, 2001, now U.S.Pat. No. 6,483,677; which is a continuation application of U.S. Ser. No.09/468,309, filed Dec. 21, 1999, now U.S. Pat. No. 6,278,593; which is acontinuation application of U.S. Ser. No. 08/626,333, filed Apr. 2,1996, now U.S. Pat. No. 6,011,674; which is a continuation applicationof U.S. Ser. No. 08/328,090, filed Oct. 24, 1994, now U.S. Pat. No.5,726,837; which is a continuation application of U.S. Ser. No.07/710,775, filed Jun. 5, 1991, now U.S. Pat. No. 5,390,061.

This invention relates to magnetoresistance effect elements using amultilayered magnetic thin film with high magnetoresistance effect, andparticularly to magnetoresistance effect elements, magnetic heads andmagnetic storage apparatus for achieving high-density recording on amagnetic recording medium on which narrow tracks are formed.

An investigation is now being made of magnetic heads using themagnetoresistance effect for high density-magnetic recording. Atpresent, an alloy film of Ni-20 at % Fe is used for themagnetoresistance effect material. However, a magnetoresistance effectelement using the Ni-20 at % Fe alloy film often causes noise such asBarkhausen noise, and thus other magnetoresistance effect materials arealso under investigation.

On the other hand, recently Suezawa, et al. have reported amagnetoresistance effect film which utilizes the ferromagneticspin-dependent tunneling phenomenon and which detects magnetic flux fromthe electrical resistance change of a multilayered film having a pair ofmagnetic layers divided by an insulating layer, as is disclose inProceedings of the International Symposium on Physics of MagneticMaterials, Apr. 8–11, 1987, pp. 303–306. This report has introduced amultilayered structure of a Ni/NiO/Co junction and multilayered films ofAl/Al₂O₃/Ni, Co-Al/Al₂O₃/Ni exhibiting the ferromagnetic spin-dependenttunneling effect. However, in either case, the junction area between thepair of magnetic layers is as wide as about 1 mm², and the relativeresistivity change, Δρ/ρ is as small as about 1% at room temperature. Inaddition, since the element structure shown in this example is notcapable of sensing a small magnetic flux change, it is impossible toprecisely detect the change of magnetic flux leaking from a magneticrecording medium recorded at a high density.

In the prior art, a Ni/NiO/Co multilayer, for example, has an Ni layerand a Co layer of a rectangular shape made perpendicular to each otherto allow all current to pass the NiO layer to effectively detect theresistance change due to the ferromagnetic spin-dependent tunnelingeffect. However, nnnnwhen used for a magnetic head, the intersection ofthe ferromagnetic Ni layer and Co layer will be insufficient toprecisely detect the magnetic field in a narrow region because thelongitudinal direction of either magnetic layer is parallel to thesurface of the magnetic recording medium. In other words, the magneticflux change associated with the signal recorded in a narrow track cannotbe detected with a high sensitivity.

Moreover, the ferromagnetic spin-dependent tunneling effect of anFe/C/Fe multilayer has been reported by J. C. Slonczewski in Phys. Rev.Vol. B39, pp. 6995, 1989, “Conductance and Exchange Coupling of TwoFerromagnets Separated by a Tunneling Barrier”.

In the application of the ferromagnetic tunneling film to the magneticheads, the ferromagnetic tunneling film is required not to deterioratein its characteristics in the course of the magnetic head producingprocess. The magnetic head producing process often includes a heatingprocess. However, when the Fe/C/Fe multilayer film is heated to 300° C.or above, carbon C is diffused into the Fe layer, thus deteriorating thecharacteristics. Also, when the intermediate layer is made of an oxidesuch as NiO or Al₂O₃, the interface energy increases in the interfacebetween the magnetic layers and the intermediate layer. The increase ofthe interface energy will act to decrease the number of atoms in theinterface, thus causing defects such as vacancies in the intermediatelayer and magnetic layer, so that the soft magnetic characteristics maybe deteriorated as described by Nakatani, et al. in J. Appl. Phys., Vol.66, pp. 4338, 1989, “Changes in Soft Magnetic Properties of FeMultilayered Films due to Lattice Mismatches between Fe and IntermediateLayers”.

Moreover, an Fe/Cr multilayered film has recently been reported, ofwhich the relative resistivity change is about 50% as described inPhysical Review Letters, Vol. 61, No. 21, pp. 2472 to 2475, 1988.

In the magnetoresistance effect element having such a multilayerstructure as the Fe/Cr multilayered film, the electrical resistance ischanged by the magnetic field when electrons are moved from a magneticlayer to another magnetic layer, or passed through a non-magneticintermediate layer. At this time, the current is flowed in thefilm-thickness direction. However, the film thickness of the magneticfilm is several hundreds of nm or below and the element resistance islow. Thus, the rate of resistance change is high, but the amount ofresistance change is small. When this film is applied to an actualmagnetic sensor or magnetic head, the output is small.

Also, in the magnetic disk apparatus, magnetic heads are used forwriting and reading information on and from a magnetic recording medium,and in this case the electromagnetic induction-type ring head, forexample, is widely used for the magnetic head for writing and reading.In a rigid-type magnetic disk apparatus for a computer, an inductioncurrent is flowed in the magnetic head which is floated with a verysmall gap from the surface of a disk-like magnetic recording mediumrotating at a high speed, so that the magnetic field generated at thetip of the magnetic head can enable recording on the magnetic recordingmedium. As the recording density is improved so that the recorded bitsare small, it has been demanded to use a magnetic head having a highwriting and reading efficiency. In the prior art, the same ring head hasbeen used for writing and reading, but no dual elements are used for aninductive-write and magnetoresistant-read dual-element magnetic head forimproving their functional efficiency. An example of this dual-elementmagnetic head is disclosed in Japanese Patent laid-open Gazette No.JP-A-51-44917. For the dual-element magnetic head, it is desired to useelements having a particularly high-sensitivity reading function, inwhich case the magnetic detecting element using the magnetoresistanceeffect (Japanese Patent Publication No. JP-B-53-17404) and the magneticdetecting element using the magnetosensitive transistor (Japanese PatentLaid-open Gazette No. JP-A-57-177573) are proposed. However, theseelements do not have enough magnetic detection sensitivity forhigh-density magnetic recording over 100Mb/in².

SUMMARY OF THE INVENTION

Accordingly, it is an object of the invention to provide amagnetoresistance effect element capable of sensing a very small changeof magnetic flux from a narrow region of a magnetic recording mediumwith high sensitivity and with high resolution.

It is another object of the invention to provide a magnetoresistanceeffect element having a high resistance to heat.

It is still another object of the invention to provide amagnetoresistance effect element of which the resistance can be greatlychanged.

It is a further object of the invention to provide a magnetic headcapable of detecting magnetic flux with high sensitivity and of beingeasy to produce, or having a simple construction.

It is still a further object of the invention to provide a magneticstorage apparatus capable of precisely writing and reading ahigh-density magnetic recording.

The inventors have studied the shape of the magnetoresistance effectelement formed of a multilayered magnetoresistance effect film which hasmagnetic layers and an intermediate layer of an insulating material suchas Al₂O₃, SiO₂, NiO or BN, a semiconductor such as Si, Ge or GaAs, or anantiferromagnetic material such as Cr, inserted between the magneticlayers, and have found that when the element is so constructed andshaped that all the current flowing in the magnetoresistance effect filmis sure to be passed through the intermediate layers and that electrodesof nonmagnetic metal (conductor) are connected at least to part of themagnetoresistance effect film, the magnetoresistance effect element candetect the magnetic field from a narrow region with high sensitivity.

The first feature of this invention is that, since at least part of themultilayered magnetoresistance effect film is formed on a conductor ofnonmagnetic metal and the film surfaces of all the magnetic layers ofthe magnetoresistance effect film are disposed substantially at rightangles to the surface of a magnetic recording medium or the end surfaceof the multilayered magnetoresistance effect film is opposed to themagnetic recording medium surface, the area of the magnetic layers ofthe end surface portion of the magnetoresistance effect film can beextremely reduced, and thus a very small change of the magnetic fluxleaking from a high-density recorded magnetic recording medium on whichnarrow tracks are formed can be detected with high sensitivity and withhigh resolution.

The magnetoresistance effect element structure according to thisinvention can be suitably formed of either one of the followingmagnetoresistance effect films (1) and (2):

(1) A multilayered film having magnetic layers and an intermediate layerof an insulating material such as Al₂O₃, SiO₂, NiO or BN, asemiconductor such as Si, Ge or GaAs, or other materials, insertedbetween the magnetic layers; for example, a ferromagnetic thin film,using a ferromagnetic spin-dependent tunneling effect, such asNi/NiO/Co, Fe/Ge/Co, Al/Al₂O₃/Ni, Co—Al/Al₂O₃/Ni, Fe—C/SiO₂/Fe—Ru,Fe—C/Al₂O₃/Co—Ni, Fe—C/Al₂O₃/Fe—Ru and so on.

(2) A multilayered film having magnetic layers and an intermediate layerof an anti-ferromagnetic material such as Cr inserted between themagnetic layers; for example, a magnetic thin film usingantiferromagnetic intermediate layers such as Fe/Cr.

Moreover, in the magnetoresistance effect element of this invention, inorder for a very small change of magnetic flux to be detected with highsensitivity and with high resolution to produce a stable reproducedoutput, the following specific technical means can be employed:

(1) The coercive force of one of a pair of magnetic layers constitutinga multilayered magnetoresistance effect film is reduced, so that thedifference between the coercive force and that of the other magneticlayer can be increased.

(2) The easy axis directions of a pair of magnetic layers constituting amultilayered magnetoresistance effect film are made perpendicular toeach other.

(3) Of a pair of magnetic layers constituting a multilayeredmagnetoresistance effect film, the angular magnetic anisotropydispersion α₉₀ of at least one magnetic layer is selected to be 10° orbelow.

(4) Of a pair of magnetic layers constituting a multilayeredmagnetoresistance effect film, at least one magnetic layer is made to bea single magnetic domain.

(5) A lamination comprised of a pair of magnetic layers and aninsulating layer constituting a multilayered magnetoresistance effectfilm is held between layers of high-permeability magnetic materials.

As described above, since the element is so constructed and shaped thatthe current flowing in the multilayered magnetoresistance effect film issure to be passed through the intermediate layer constituting themagnetoresistance effect film, and since for example at least a part ofthe magnetoresistance effect film is formed on a conductor ofnonmagnetic metal, the magnetic field from a narrow region can bedetected. In other words, when at least a part of the magnetoresistanceeffect film is formed on an electrode conductor of nonmagnetic metal,the film surfaces of all the magnetic layers constituting themagnetoresistance effect film can be opposed substantially at rightangles to the magnetic recording medium surface. Thus, since the area ofthe magnetic layers of the end surface portion of the magnetoresistanceeffect film facing the magnetic recording medium can be extremelyreduced, the magnetic field from a narrow region can be detected with ahigh sensitivity. In addition, either one of the multilayeredmagnetoresistance effect films, or (1) the magnetic thin film using theferromagnetic spin-dependent tunneling effect and (2) the magnetic thinfilm using the antiferromagnetic intermediate layers, can be applied tothe element structure of this invention.

Moreover, in order for, for example, one of a pair of magnetic layersconstituting the multilayered magnetoresistance effect film to bechanged in its magnetization direction by the magnetic field leakingfrom the medium, the coercive force is set to about the leaked magneticfield strength. Also, in order for the other magnetic layer not to bechanged in its magnetization direction even if the leaked magnetic fieldfrom the medium is applied thereto, the coercive force is set to asufficiently high value.

If the coercive forces of the pair of magnetic layers are set as above,it is possible to obtain an output that is higher than in theconventional inductive-type thin-film head or magnetoresistance effecthead.

Moreover, the magnetic layer which is changed in its magnetizationdirection by the magnetic field leaking from the medium is required tohave a small angular magnetic anisotropy dispersion and a singlemagnetic domain in order that the magnetization rotation is caused at atime. If this condition is satisfied, the reading sensitivity andstability can be improved.

Moreover, the total film thickness of the multilayered magnetoresistanceeffect film comprised of a pair of magnetic layers and an insulatinglayer is reduced to be smaller than the shortest recorded bit lengthwritten on the medium, and the multilayered magnetoresistance effectfilm is held between a pair of high-permeability films, thereby furtherimproving the reading resolution.

In addition, since the junction area between a pair of magnetic layersconstituting the multilayered magnetoresistance effect film is reduced,the probability of the occurrence of defects (pinholes) in theinsulating layer can be reduced, so that the reproduction sensitivitycan be further improved.

The second feature of the invention is that even if the coercive forcesof the two magnetic layers of the ferromagnetic spin-dependent tunnelingeffect film constituting the magnetoresistance effect element are notgreatly different (e.g. if the materials of the two layers are thesame), application of a bias magnetic field from an antiferromagneticmaterial to one magnetic layer will enable the magnetic field forchanging the magnetization direction of the layer to change, so that themagnetization directions of both layers are antiparallel in a certainrange of magnetic field, but are parallel in another range of magneticfield, thus the element exhibiting the magnetoresistance effect.

Moreover, since at least a part of the ferromagnetic spin-dependenttunneling effect film is formed on nonmagnetic metal, the area of themagnetic layers facing the magnetic recording medium can be decreased,so that the magnetic field from a narrow region can be detected.

As described above, even if the coercive forces of the two magneticlayers of the ferromagnetic tunneling effect film are not greatlydifferent (e.g. if the materials of the two layers are the same),application of a bias magnetic field from the antiferromagnetic materialto one magnetic layer will enable the magnetic field for changing themagnetization directions of both layers to change. Thus, themagnetization directions of both layers are antiparallel in a certainrange of magnetic field, but are parallel in another range of magneticfield, thus the element exhibiting the magnetoresistance effect.

Moreover, since at least a part of the ferromagnetic tunneling effectfilm is formed on nonmagnetic metal, the area of the magnetic layersfacing the magnetic recording medium can be decreased, so that themagnetic field from a narrow region can be detected.

The third feature of the invention is that, since after the study on themultilayered film exhibiting the ferromagnetic spin-dependent tunnelingeffect, one or more materials for an intermediate layer are selectedfrom a carbide, a boride, a nitride, a phosphide and a compound of groupIIIb to Vb elements, the soft magnetic characteristics of the magneticlayers are not deteriorated and the characteristics of the ferromagneticspin-dependent tunneling element are not changed even when the elementis passed through the heating process for magnetic head production.

In other words, when an oxide intermediate layer of NiO or Al₂O₃ isused, the interface energy is increased in the interface between themagnetic layers and intermediate layer. When the interface energy ishigh, the number of atoms in the interface tends to decrease, anddefects may occur, such as vacancies from which atoms are ejected, sothat the soft magnetic characteristics may be deteriorated as describedby Nakatani, et al. in J. Appl. Phys., Vol. 66, pp. 4338, 1989, “Changesin Soft Magnetic Properties of Fe Multilayered Films due to LatticeMismatches between Fe and Intermediate Layers”. On the other hand, theintermediate layer of a carbide, a boride, a nitride, a phosphide or acompound of group IIIb to Vb elements has a low interface energy betweenthe magnetic layers. Therefore, the number of atoms in the interface maybe large, and thus no defect occurs in the magnetic layers. Moreover,the compound intermediate layer has a high melting point and thus if theelement is passed through the heating process for magnetic headproduction, the elements of the intermediate layer are not diffused intothe magnetic layers, so that the ferromagnetic tunneling effect elementis not deteriorated. Also, since the intermediate layer is used to formthe tunneling junction, it is necessary for it to be made of aninsulating material or to have an electrical resistance higher than thatof the semiconductor.

In summary, as described above, the intermediate layer of carbide, aboride, a nitride, a phosphide or a compound of group IIIb to Vbelements has a low interface energy between the magnetic layers.Therefore, no defect occurs in the magnetic layers. Moreover, thecompound intermediate layer has a high melting point and thus if theelement is passed through the heating process for the magnetic headproduction, the elements of the intermediate layer are not diffused intothe magnetic layers, so that the ferromagnetic tunneling effect elementis not deteriorated.

The fourth feature of the invention is that, since after the study onthe element using the Fe/Cr multilayered film and the element having themagnetoresistance effect due to the multilayered structure such as theferromagnetic tunneling element, it has been found that the resistancesof these elements are low so that a large amount of resistance changecannot be obtained even when the relative resistivity change is high, orthat in the element having the Fe/Cr multilayered films and the elementhaving the magnetoresistance effect due to the multilayered structuresuch as the ferromagnetic tunneling element, the electrical resistanceof the whole element can be increased by series connection of aplurality of magnetoresistance effect elements, and that the element isso constructed that electrons are passed a plurality of times throughthe nonmagnetic layer located at the same distance from the base.

As described above, in the element having the Fe/Cr multilayered filmsand the element having the magnetoresistance effect due to themultilayered structure such as the ferromagnetic tunneling element, theelectrical resistance of the whole element can be increased and a largeamount of resistance change can be obtained by series connection of aplurality of magnetoresistance effect elements. Also, since the elementis so constructed that electrons are passed a plurality of times throughthe nonmagnetic layer located at the same distance from the substrate,the electrical resistance of the whole element can be increased and alarge amount of resistance change can be obtained without increasing thefilm thickness of the whole element. Moreover, according to thisinvention, since the film thickness of the whole element is not changed,the resolution relative to the magnetic field distribution in thewavelength direction is not reduced when the element is used in amagnetic head.

The fifth feature of the invention is that, as an element for detectingthe magnetic flux leaking from the magnetic domain recorded on amagnetic recording medium, a plurality of ferromagnetic laminatedelements connected in series through a very thin electrically insulatingfilm, semiconductor film or semimetal film can be used in a magnetichead to detect the phenomenon that the tunneling current flowing throughthe element upon supplying current thereto is changed in accordance withthe change of the magnetic field.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a perspective view of the structure of a magnetoresistanceeffect element of a first embodiment of the invention.

FIG. 2 is a graph showing the relation between the applied magneticfield and the relative resistivity change of the magnetoresistanceeffect element.

FIGS. 3 and 4 are perspective views of the structure of amagnetoresistance effect element of a second embodiment of theinvention.

FIGS. 5A, 5B and 5C are diagrams showing manufacturing processes for amagnetoresistance effect element.

FIG. 6 is a graph showing the hysteresis characteristic of amagnetoresistance effect element produced by the processes shown inFIGS. 5A, 5B and 5C.

FIG. 7 is a graph showing the constant applied magnetic field vs.relative resistivity change of a magnetoresistance effect elementproduced by the processes shown in FIGS. 5A, 5B and 5C.

FIG. 8 is a graph showing the relation between the angular magneticanisotropy dispersion α₉₀ and the rate of resistance of amagnetoresistance effect element produced by the processes shown inFIGS. 5A, 5B and 5C.

FIG. 9 is a graph showing the relation between the frequency and therelative resistivity change of a magnetoresistance effect elementproduced by the processes shown in FIGS. 5A, 5B and 5C.

FIG. 10 is a cross-sectional diagram of the writing/reading dual-elementmagnetic head having a magnetoresistance effect element formed on theinduction-type thin-film head.

FIG. 11 is a graph showing the comparison of the reading characteristicof the magnetic head shown in FIG. 10 with the conventionalinduction-type thin-film head.

FIGS. 12 and 13 are perspective views of the structures of theconventional magnetoresistance effect elements.

FIG. 14A is a side view of the structure of the ferromagnetic tunnelingfilm of a magnetoresistance effect element of a third embodiment of theinvention.

FIG. 14B is a side view of the structure of the ferromagnetic tunnelingfilm of a magnetoresistance effect element of a fifth embodiment of theinvention.

FIG. 15 is a graph showing the magnetization of the ferromagnetictunneling film.

FIG. 16 is a perspective view of the structure of a magnetoresistanceeffect element of the third embodiment of the invention.

FIG. 17 is a graph showing the relation between the applied magneticfield and the rate of resistance change of a magnetoresistance effectelement.

FIG. 18 is a perspective of the structure of a magnetoresistance effectelement of a sixth embodiment of the invention.

FIG. 19 is a graph showing the relation between the applied magneticfield and the relative resistivity change of a magnetoresistance effectelement.

FIGS. 20A, 20B, 20C, 20D and 20E are perspective views showing themanufacturing processes of a magnetoresistance effect element using theFe/Cr multilayered films in an eighth embodiment of the invention.

FIG. 21 is a perspective view of a structure of a magnetoresistanceeffect element using conventional Fe/Cr multilayered films as acomparing example.

FIG. 22 is a graph showing the applied magnetic field vs. relativeresistivity change of a magnetoresistance effect element of theinvention and of the conventional one for comparison.

FIG. 23 is a perspective view of the ferromagnetic tunneling structureof a magnetoresistance effect element of a ninth embodiment of theinvention.

FIG. 24 is a cross-sectional diagram showing the ferromagnetic tunnelingstructure.

FIGS. 25A and 25B are diagrams useful for explaining the principle ofthe operation of a magnetic head of the invention.

FIG. 26 is a graph showing the principle of the operation of a magnetichead.

FIGS. 27A and 27B are cross-sectional views of a magnetic head.

FIGS. 28A, 28B and 28C are cross-sectional diagrams showing themanufacturing process of a magnetic head.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

Embodiments of the invention will be described with reference to thedrawings.

FIG. 1 is the structure of one embodiment of a magnetoresistance effectelement of the invention.

The magnetoresistance effect film using the magnetoresistance effectelement and the Cu electrode were produced by an ion beam sputteringapparatus under the following conditions:

Ion gas Ar Ar gas pressure within apparatus 2.5 × 10⁻² Pa Accelerationvoltage of ion gun 400 V for evaporation Ion current of ion gun for 60mA evaporation Distance between target and 127 mm substrates

The magnetoresistance effect film and Cu electrode were shaped by ionmilling, and Corning-7059 glass was used for the substrate.

The process for producing the magnetoresistance effect element shown inFIG. 1 will be described below. First, a Cu film is formed on a glasssubstrate by ion beam sputtering and worked to be a Cu electrode 1 of arectangular shape of 8-μm width, 2-mm length by ion milling. Leveldifferences, or steps, caused by the working are flattened with a resin.Then, a 100-nm thick Fe-1.3 at % Ru alloy layer 2, a 10-nm thick SiO₂layer 3 and a 100-nm thick Fe-1.00 at % C alloy layer 4 are deposited inturn by ion beam sputtering. These layers are worked to be a rectangularof 5-μm width, 20-μm length by the ion milling, thus producing amagnetoresistance effect film 5. Level differences, or steps, caused bythis working are flattened with a resin. Moreover, a Cu thin film isformed on this film by ion sputtering and worked to be a rectangular Cuelectrode 6 of 8-μm width, 2-μm length. Current is flowed between the Cuelectrode 1 and the Cu electrode 6, and the change of the voltagethereacross is measured so that the change of the electrical resistanceis detected. In this case, the current particularly flows through theSiO₂ layer 3.

When a magnetic field was applied to the magnetoresistance effect film 5in the longitudinal direction by use of a Helmholtz coil and the changeof the electrical resistance examined, FIG. 2 shows the relation betweenthe magnetic field and the electrical resistance. As illustrated, theelectrical resistance of the element changes with the magnitude of themagnetic field. The maximum relative resistivity change is about 1%.This value is substantially the same as that of the Ni/Nio/Comultilayered film described in one of the above citations, but themagnetic field intensity at which the electrical resistance is themaximum, in the magnetoresistance effect element of the invention, islower than in the prior art. Therefore, the element according to thisinvention is very advantageous when used for the magnetic head.

The cause of this resistance change will be considered as follows. Bythe measurement of the magnetization curves, it was found that thecoercive force of the Fe-1.3 at % Ru alloy layer 2 was 25 Oe and thatthe coercive force of the Fe-1.0 at % C alloy layer 4 was 8 Oe. When themagnetic field strength is changed, the direction of the magnetizationof the Fe-1.0 at % C alloy layer 4 changes, but that of the Fe-1.3 at %Ru alloy layer 2 does not change. However, when a magnetic field of 25Oe is applied, the direction of the magnetization of the Fe-1.3 at % Rualloy layer 2 is changed. Thus, under the application of a field of ±8to 25 Oe, the magnetization directions of the Fe-1.0 at % C alloy layer4 and Fe-1.3 at % Ru alloy layer 2 are antiparallel, when the fieldstrength is out of the above range, the magnetization directions areparallel. Accordingly, since the tunneling current flowing in the SiO₂layer 3, causes the conductance to become higher when the magnetizationdirections of the magnetic layers are parallel than when themagnetization directions are antiparallel, the electrical resistance ofthe element changes with the magnitude of the magnetic field.

To further illustrate the present embodiment, a ferromagnetic tunnelingelement, having the same shape as in the prior art shown in FIG. 12, isformed of the Fe-1.3 at % Ru alloy layer 2 of 5-μm width, 100-nmthickness, the SiO₂ layer 3 of 10-nm thickness, and the Fe-1.0 at % Calloy layer 4 of 5-μm width, 100-nm thickness. The Fe-1.3 at % Ru alloylayer 2 and the Fe-1.0 at % C alloy layer 4 are perpendicular to eachother.

The magnetoresistance effect element of the same shape as in the priorart has the same magnetic layers as the magnetoresistance effect element(FIG. 1) of the present invention mentioned above, and thus exhibitssubstantially the same resistance change with the magnetic fieldstrength as does the element shown in FIG. 1.

When the magnetic field from the magnetic recording medium is detectedby these elements, the magnetoresistance effect element of the invention(FIG. 1) is capable of reading a track of 5-μm width by facing the endof the rectangular magnetoresistance effect film 5 of 5-μm width and20-μm length to the magnetic recording medium. However, in themagnetoresistance effect element of the same shape as in the prior art(FIG. 12), the tunneling junction 7, which is greatly concerned with themagnetoresistance effect, is formed at the center between the Fe-1.0 at% C alloy layer 4 and the Fe-1.3 at % Ru alloy layer 2, and thus cannotbe faced to the magnetic recording medium.

Thus, for the description of this embodiment, a magnetoresistance effectelement of the conventional structure shown in FIG. 13 may be produced.This element is formed of the Fe-1.3 at % Ru alloy layer 2 of 5-μmwidth, 100-nm thickness, the SiO₂ layer 3 of 10-nm thickness, and theFe-1.0 at % C alloy layer 4 of 5-μm width, 100-nm thickness. The Fe-1.0at % C alloy layer 43 is cut off at the tunneling junction 7, and thusthe tunneling junction 7 can be faced to the magnetic recording medium.However, in the structure of FIG. 13, the longitudinal direction portionof the Fe-1.3 at % Ru alloy layer 2 is faced to the magnetic recordingmedium and thus affected by the magnetic field leaked from the magneticrecording medium. Therefore, even if the width of the Fe-1.0 at % Calloy layer 4 is selected to be 5 μm, the effective track width is muchgreater than 5 μm.

According to the structure of the element of the invention, as describedabove, at least part of the magnetoresistance effect film is formed on anonmagnetic metal conductor, and the magnetoresistance effect films areoverlapped in a straight line so that the current can completely flowthrough the intermediate layer. Thus, the longitudinal (film surface)directions of all the magnetic layers of the magnetoresistance effectfilm are made substantially perpendicular to the magnetic recordingmedium surface, making it possible to extremely reduce the area of themagnetic layer at the end of the magnetoresistance effect film opposingthe magnetic recording medium, and to detect the magnetic field leakedfrom narrow regions with high sensitivity.

While in this embodiment the Fe-1.3 at % Ru alloy layer 2 and the Fe-1.0at % C alloy layer 4 are used as the magnetic layers, and the SiO₂ layer3 is used as the intermediate layer, other magnetic materials andinsulating materials may be used for the magnetic layers andintermediate layer, in which case the same effect can of course beachieved.

FIG. 3 shows the structure of a second embodiment of a magnetoresistanceeffect element of the invention.

The magnetoresistance effect element having the structure shown in FIG.3 will be described in the same way as in the first embodiment. Theprocess for this magnetoresistance effect element will also be describedbelow. First, the Fe-1.3 at % Ru alloy layer 2 of 5-μm width, 8-μmlength and 100-nm thickness is formed on the rectangular Cu electrode 1of 8-μm width and 2-mm length. Then, the SiO₂ layer 3 is deposited tocover all of the Fe-1.3 at % Ru alloy layer 2. Also, the Fe-1.0 at % Calloy layer 4 of 5-μm width, 100-nm thickness is formed to cover all ofthe SiO₂ layer 3. A current is flowed between the Cu electrode 1 and theFe-1.0 at % C alloy layer 4 and the voltage thereacross is measured.

In the magnetoresistance effect element shown in FIG. 3, all of thecurrent is flowed in the intermediate layer, and thus themagnetoresistance effect can be effectively utilized. Also, themagnetoresistance effect films can be overlapped in a straight line, andthe longitudinal (film surface) direction of all the magnetic layers ofthe end surfaces of the magnetoresistance effect films can be madeperpendicular to the magnetic recording medium surface. Thus, the areaof the magnetic layers at the end surfaces of the magnetoresistanceeffect films opposite to the magnetic recording medium can be extremelyreduced so that the magnetic field from a narrow region can be detectedwith high sensitivity.

In addition, the construction of an element shown in FIG. 4 can beconsidered to have the same effect as the magnetoresistance effectelement shown in FIG. 3. As illustrated, the Fe-1.3 at % Ru alloy layer2, the SiO₂ layer 3, and the Fe-1.0 at % C alloy layer 4 are formed onthe large-area Cu electrode 1. That is, the Fe-1.3 at % Ru alloy layer2, the SiO₂ layer 3, and the Fe-1.0 at % C alloy layer 4 are formed onthe large-area Cu electrode 1. The level differences, or steps, areflattened with a resin or the like, and the Cu electrode 6 is formed tobe in contact with the Fe-1.0 at % alloy layer 4.

While in this embodiment the Fe-1.3 at % Ru alloy layer 2 and the Fe-1.0at % C alloy layer 4 are used as the magnetic layers, and the SiO₂ layer3 is used as the intermediate layer, the magnetic layers andintermediate layer may be made of other magnetic materials andinsulating materials, respectively, in which case the same effect can beachieved.

Another embodiment of a magnetoresistance effect element of theinvention will be described below. The magnetoresistance effect film 5of the magnetoresistance effect element shown in FIG. 1 is formed of anFe(3nm)/Cr(1nm) multilayered film (100 nm thick).

A magnetic field from a Helmholtz coil was applied to themagnetoresistance effect film 5 in the longitudinal direction, and therelative resistivity change was examined. The result was that, in theelement of this embodiment, the resistivity of the element changes withthe magnitude of the magnetic field and the maximum relative resistivitychange is about 10%.

A description will be made of the process for producing the readingmagnetic heads using the magnetoresistance effect elements of the aboveembodiments, the measured relative resistivity change, and the readingsensitivity with which the recorded signal actually written on themagnetic recording medium is read, as compared with those of theconventional magnetoresistance effect-type (MR) head and induction-typethin-film head.

FIGS. 5A, 5B and 5C are useful for explaining the process for producingthe head. First, the Cu layer for a lower electrode 9 is deposited on asubstrate 8 by sputtering. Then, a Co—Ni-based magnetic layer of highcoercive force Hc=2000 Oe is deposited thereon to a thickness of 0.1 μmby sputtering to form a lower magnetic pole 10. This lower magnetic pole10, after being deposited, is patterned to be 3 μm wide and 3 μm long bythe normal photoresist process. Thereafter, an insulating layer 11 ofAl₂O₃ is deposited thereover to a thickness of 50 Å by the samesputtering method.

Then, a magnetic layer for an upper magnetic pole 12 is deposited bysputtering, which layer is made of an Fe-based alloy having a saturationmagnetic flux density Bs=2.0 T, coercive force 0.3 Oe and angularmagnetic anisotropy dispersion α₉₀ 5° or below.

In the above embodiments, the upper magnetic pole 12 is made of an Fe—Calloy. This magnetic layer should have a single magnetic domain forstabilizing the reading characteristics. For this purpose, a BNintermediate layer is inserted in the magnetic layers.

The upper magnetic pole 12 is patterned to be 2 μm wide and long. Afterthe patterning, a resist 13 is coated on the upper magnetic pole 12, anda through-hole is formed therein. Then, an upper electrode 14 throughwhich a current is supplied to the upper magnetic pole 12 is formed,completing the process.

FIG. 6 shows the hysteresis characteristics of the device. From FIG. 6,it will be seen that the difference between the coercive forces of apair of magnetic layers appears clearly. The coercive forces of thepaired magnetic layers are 50 Oe and 400 Oe, respectively. Within therange from 50 Oe to 400 Oe, the amount of magnetization of the magneticlayers is almost not changed with the change of the external magneticfield, and the paired magnetic films are quite separately changed inmagnetization as will be understood from FIG. 6. The difference betweenthe coercive forces of the paired magnetic layers is set to a propervalue depending on the coercive force and saturation magnetization ofthe medium to be used, so that the reading sensitivity to the externalmagnetic field can be increased.

FIG. 7 shows the measured result of the relative resistivity change to auniformly applied magnetic field. Although the measurement was made atroom temperature, the relative resistivity change Δρ/ρ is as high as 5%.The easy axis direction between the pair of anisotropic magnetic layerswas 90° and the external magnetic field was applied in the easy axisdirection of the magnetic layer having the higher coercive force.

FIG. 8 shows the measured result of the relative resistivity change withthe gradual decrease of the angular magnetic anisotropy dispersion anglefrom 70°. From FIG. 8, it was confirmed that the better results can beobtained for smaller angular dispersions α_(π). However, under thepresent technique, the angular dispersion is limited to about 5 degreesat which the relative resistivity change Δρ/ρ is 5%. If the angulardispersion is limited to about 10 degrees, the relative resistivitychange can be set to 4.8% or above. Thus, in this embodiment, theangular dispersion is set to within 5 to 10 degrees. Also, the samplewas cut in one direction by mechanical abrasion, a normal thin film headwas pressed onto the abraded surface of the sample, and the relativeresistivity change in a high frequency region was measured. FIG. 9 showsthe result. From FIG. 9, it was confirmed that the relative resistivitychange is substantially flat up to 30 MHz.

In addition, the magnetoresistance effect elements according to thefirst and second embodiments were attached on inductive thin-film headsto form an inductive-write and magnetoresistant-read dual-element head,and the reading characteristics were measured. FIG. 10 shows thecross-sectional structure of the dual-element head. Here, in order toincrease the resolution to the external magnetic field, shield layers15, 16 are provided on both sides of the multilayered film which isformed of a pair of magnetic layers and a nonmagnetic intermediatelayer, as shown in FIG. 10. The distance between the shield layers 15and 16 is 0.3 μm.

The reading characteristic of this magnetic head combined with a 500 Åsputtered medium having a coercive force of 2000 Oe was measured andcompared with the induction-type thin-film head and the MR head. FIG. 11shows the compared result of the reading sensitivity of each head, inwhich the abscissa is the recording density and the ordinate is thereading output per unit track width. In this measurement, the spacingwas 0.15 μm. From the result, it was confirmed that the reading outputof the magnetic head according to the invention is 2.5 times as large asthat of the inductive head, and about 1.3 times as large as that of theMR head. Moreover, the variation of reading output as measured in the MRhead was not observed at all.

Thus, according to the first feature of the invention, in themagnetoresistance effect element using a multilayered magnetoresistanceeffect film which is formed on magnetic layers and a semiconductor orantiferromagnetic intermediate layer inserted between the magneticlayers, all the current flowing in the magnetoresistance effect film issure to pass through the intermediate layer, at least part of themagnetoresistance effect film is formed on a conductor made of anonmagnetic metal, and the film surface directions of all the magneticlayers of the magnetoresistance effect film are made to be substantiallyperpendicular to the magnetic recording medium surface so that themagnetic field can be detected. Thus, the area of the magnetic layer ofthe end face of the magnetoresistance effect film opposite to themagnetic recording medium can be extremely reduced, and the magneticfield leaked from the narrow regions of the high-density magneticrecording medium having narrow tracks can be detected with highsensitivity.

Moreover, the magnetoresistance effect film having the multilayeredstructure may be either of:

(1) A magnetic thin film using the ferromagnetic spin-dependenttunneling effect, and

(2) A magnetic thin film using the antiferromagnetic intermediate layer.

In addition, the reading magnetic head using the magnetoresistanceeffect element, even for a track width of, for example, 2 μm or below,can produce a stable output with a high S/N ratio, and thus it isextremely useful as the head of a magnetic disk apparatus which has alarge storage capacity and requires high speed transfer of data.

FIG. 14A shows the structure of a third embodiment of amagnetoresistance effect element of the invention.

The ferromagnetic spin-dependent tunneling effect film which constitutesthe magnetoresistance effect element is formed by an ion beam sputteringapparatus under the following conditions:

Ion gas Ar Ar gas pressure within the 2.5 × 10⁻² Pa apparatusAcceleration voltage of ion gun 1200 V for evaporation Ion current fromion gun for 120 mA evaporation Distance between target and 127 mmsubstrates

Corning-7059 glass was used for the substrate. The ferromagnetictunneling effect film in this embodiment was produced by forming on asubstrate 31 of a 100-nm thick lower magnetic layer 32 of Fe-1.0 at % Calloy, a 10-nm thick intermediate layer 33 of Al₂O₃, a 100-nm uppermagnetic layer 34 of Fe-1.0 at % C alloy, and a 50-nm thickantiferromagnetic layer 35 of Cr in turn. The ferromagnetic tunnelingeffect film shown in FIG. 14B is similar but, as discussed more fullybelow, includes an Ni-20 at % Fe alloy layer 5-nm thick between theFe-1.0 at % C alloy and the Fe-50 at % Mn alloy.

The magnetization curve of the ferromagnetic tunneling effect film wasmeasured at a temperature of 4.2 K by a B-H curve tracer. FIG. 15 showsthe measured magnetization curves. As shown in FIG. 15, the coerciveforces of the lower magnetic layer 32 and the upper magnetic layer 34are equally 7 Oe. However, a bias field is applied from theantiferromagnetic layer 35 to the upper magnetic layer 34, so that themagnitude of the magnetic field changing in the magnetization directionis shifted to the high magnetic field side. Therefore, when the magneticfield is increased from the negative to the positive side, themagnetization directions of the lower magnetic layer 32 and the uppermagnetic layer 34 are antiparallel within the magnetic field range of 7to 24 Oe, but are parallel within the other range. When the magneticfield is decreased from the positive to the negative side, themagnetization directions of the lower magnetic layer 32 and the uppermagnetic layer 34 are antiparallel within the magnetic field range of −7to 10 Oe, but are parallel within the other range.

It is considered that in the magnetic field in which the magnetizationdirections are antiparallel, the electrical resistance of theferromagnetic tunneling effect film is high, but in the field in whichthe magnetization directions are parallel, the electrical resistance islow.

Thus, to examine the change of resistance of the ferromagnetic tunnelingeffect film, an element was produced as shown in FIG. 16. The processfor producing this element will be described below. First, a Cuelectrode 36 10 μm wide and 100 nm thick is formed on a nonmagneticsubstrate by ion beam sputtering and ion milling. Then, on the Cuelectrode 36, there are formed a 10 μm×10 μm×100-nm thick lower magneticlayer 37 of Fe-1.0 at % C alloy, a 10 μm×10 μm×10 nm thick intermediatelayer 38 of Al₂O₃, a 10 μm×10 μm×100-nm thick upper magnetic layer 39 ofFe-1.0 at % C alloy, and a 10 μm×10 μm×50-nm thick antiferromagneticlayer 40 of Cr, in turn. Thereafter, the level differences, or steps,are flattened with a resin, and a Cu electrode 41 is formed to be incontact with the surface of the antiferromagnetic layer 40.

A magnetic field was applied to the Cu electrodes in the directionperpendicular to the longitudinal direction by use of a Helmholtz coil,and the change of electrical resistance was examined. The measurementwas made at a temperature of 4.2 K. FIG. 17 shows the relation betweenthe magnetic field and the electrical resistance. From FIG. 17, it willbe seen that the electrical resistance of the element is changed withthe magnitude of the magnetic field. The maximum relative resistivitychange was about 3.6%.

The magnetic field strength at which the electrical resistance is themaximum is about 0 Oe and 16 Oe and thus lower than that of theconventional ferromagnetic tunneling effect film. This is because themagnetoresistance tunneling effect film of the embodiment is formed ofonly relatively low-coercive force magnetic layers. In the conventionalferromagnetic tunneling effect film, though, the coercive forces of thetwo magnetic layers must be different, and thus the magnetic field atwhich the element operates is large. On the other hand, since theferromagnetic tunneling effect film of this embodiment is operated undera low magnetic field, the magnetoresistance effect element using thisfilm is advantageous to the magnetic head as compared with theconventional one.

Moreover, the ferromagnetic tunneling effect film of this embodiment isformed on only a soft magnetic film. The soft magnetic film has a smallmagnetic anisotropy dispersion, and thus the magnetization direction ofvery small portions of each magnetic layer is just at an angle for theparallel or antiparallel, but difficult at an intermediate angle. Sincethe ferromagnetic spin-dependent tunneling effect depends on thedirection of the magnetization of each magnetic layer, the magnetizationis difficult at an intermediate angle. Thus, a ferromagnetic tunnelingeffect film formed on only a soft magnetic film as in this embodimenthas a relatively large relative resistivity change.

Also, as in this embodiment, when at least part of the magnetoresistanceeffect film is formed on a nonmagnetic metal, all the current is passedthrough the intermediate layer, thus effectively detecting themagnetoresistance effect. Moreover, in the application to the magnetichead, if, as in this embodiment, at least part of the magnetoresistanceeffect film is formed on a nonmagnetic metal, the cross-sectional areaof the magnetic layer facing the magnetic recording medium can bereduced so that the magnetic field from a narrow region can be detected.

In addition, while in this embodiment, the magnetic layers are formed ofFe-1.0 at % C alloy and the intermediate layer is formed of Al₂O₃, themagnetic layers and the intermediate layer may be formed on othermagnetic materials and insulating material, respectively, in which casethe same action can be achieved. If the antiferromagnetic layer is madeof an antiferromagnetic material having a Néel point above thetemperature at which the magnetoresistance effect is measured, themagnetoresistance effect can be achieved.

Also, while in this embodiment the antiferromagnetic layer is formed onthe upper magnetic layer, it may be formed on the lower magnetic layerin which case the same effect can be achieved.

As a fourth embodiment of a magnetoresistance effect element of theinvention, a magnetoresistance effect element was produced in the sameway as in the third embodiment. The magnetic layers were Fe-1.0 at % Calloy and the intermediate layer was Al₂O₃. The antiferromagnetic layerwas Cr-1 at % Ru alloy and Cr-25 at % Au alloy. The relative resistivitychange of the magnetoresistance effect element of this embodiment was1.5% at room temperature when the Cr-1 at % Ru alloy was used, and 1.8%when the Cr-25 at % Au alloy was used. In addition, the electricalresistance was the maximum when the magnetic field was substantially thesame as in the element of the third embodiment.

FIG. 14B illustrates a fifth embodiment of a magnetoresistance effectelement of the invention wherein, a magnetoresistance effect element wasproduced in the same way as in the third embodiment. The magnetic layers32, 34 a were Fe-1.0 at % C alloy and the intermediate layer 33 wasAl₂O₃. The antiferromagnetic layer 35 was Fe-50 at % Mn alloy. Moreover,a Ni-20 at % Fe alloy layer 34 b 5 nm thick was provided between theFe-1.0 at % C alloy layer 34 a and the Fe-50 at % Mn alloy layer 35. Thereason for this is as follows.

When the Fe-50 at % Mn alloy layer 35 is formed on a body-centered cubicstructure material, it easily forms an α-phase structure. The Néeltemperature of the Fe—Mn-based alloy of the α-phase structure is lowerthan room temperature. On the contrary, the Fe-50 at % Mn alloy layer 35easily forms a γ-phase structure when formed on a face-centered cubicstructure. The Néel temperature of the γ-phase-structured Fe—Mn-basedalloy is higher than room temperature. Therefore, in order to obtain amagnetoresistance effect element operating at room temperature, an Ni-20at % Fe alloy layer 34 b of face-centered cubic structure was providedbetween the Fe-1.0 at % C alloy layer 34 a and the Fe-50 at % Mn alloylayer 35.

The relative resistivity change of the magnetoresistance effect elementof this embodiment was 1.6% at room temperature. The electricalresistance was the maximum when the magnetic field was substantially thesame as in the element of the third embodiment.

As described in detail above, according to the second feature of theinvention, even if the coercive forces of the two magnetic layers of theferromagnetic tunneling effect film are not greatly different (e.g., thematerials of the two layers are the same), application of a biasmagnetic field from the antiferromagnetic material to one magnetic layerwill change the magnetic field for changing the magnetization directionsof the layer, thus providing the magnetoresistance effect. Moreover, ifat least part of the ferromagnetic tunneling effect films formed on thenonmagnetic metal, the area of the magnetic layer facing the magneticrecording medium can be reduced, so that the magnetic field from anarrow region can be detected.

FIG. 18 shows the structure of a sixth embodiment of a magnetoresistanceeffect element of the invention. A ferromagnetic tunneling effectelement constituting the magnetoresistance effect element was producedby an ion beam sputtering apparatus under the following conditions:

Ion gas Ar Ar gas pressure within the 2.5 × 10⁻² Pa apparatus Ion gunacceleration voltage 1200 V for evaporation Ion gun ion current for 120mA evaporation Distance between target 127 mm and substrates

Corning-7059 glass was used for the substrate.

The ferromagnetic tunneling effect element constituting themagnetoresistance effect element of this embodiment is produced byforming on the substrate a 100-nm thick lower electrode 51 of Cu, a100-nm thick lower magnetic layer 52 of Fe-1.7 at % Ru alloy, a 10-nmthick intermediate layer 53 of BN, a 100-nm thick upper magnetic layer54 of Fe-2.0 at % C alloy, and a 100-nm thick upper electrode 55 of Cu,in turn. The working of each layer was performed by ion milling.

The resistivity change of the ferromagnetic tunneling effect elementwith the change of the magnetic field was measured at a temperature of4.2 K. A current was flowed between the upper electrode 55 and the lowerelectrode 51, and the voltage between the electrodes was measured todetect the resistivity change.

FIG. 19 shows the measured result. From FIG. 19, it will be seen thatthe electrical resistance of the element changes with the magnitude ofthe magnetic field. The maximum rate of change was about 5.1%. Themagnitude of the magnetic field at which the electric resistance is themaximum is −15 Oe and 16 Oe. These values are substantially intermediatebetween the coercive force of 10 Oe of the upper magnetic layer 54 andthe coercive force of 21 Oe of the lower magnetic layer 52.

The magnetic layer of the ferromagnetic tunneling effect element of thisembodiment is formed of only an Fe-based alloy film. The Fe-based alloyfilm has a large polarization in the band structure and theferromagnetic tunneling effect element has a relatively high relativeresistivity change.

Moreover, if as in this embodiment, at least part of the ferromagnetictunneling element is formed on a nonmagnetic metal, all the current flowis passed through the intermediate layer, thus effectively detecting theferromagnetic tunneling effect. Also, in the application to the magnetichead, if at least part of the ferromagnetic tunneling effect element isformed on a nonmagnetic metal as in this embodiment, the cross-sectionalarea of the magnetic layer opposing to the magnetic recording medium canbe reduced, so that the magnetic field from a narrow region can bedetected.

Moreover, while in this embodiment, the magnetic layers were made ofFe-1.7 at % Ru alloy and Fe-2.0 at % C alloy, the magnetic layers may bemade of other magnetic materials, in which case the same effect can beachieved.

As a seventh embodiment of a magnetoresistance effect element of theinvention, a ferromagnetic tunneling effect element was produced in thesame way as in the sixth embodiment. The magnetic layers were made ofthe same alloy materials as in the fifth embodiment and the intermediatelayer was made of another compound than the C-alloy, oxide NiO, Al₂O₃and the oxide according to this invention. The ferromagnetic tunnelingeffect element was produced at a temperature of 200 to 400° C.

Intermediate layer Production temperature material 200° C. 300° C. 400°C. Prior C 5.2% 2.6% 0.0% art NiO 3.8% 1.5% 0.0% Al₂O₃ 3.5% 3.6% 3.5%This BN 5.1% 5.3% 5.0% invention B₄C 5.2% 5.5% 5.0% AlP 4.8% 5.0% 5.0%GaAs 4.6% 4.8% 5.0%

As listed in Table 1, at a production temperature of 200° C., theferromagnetic tunneling element using the intermediate layer of othermaterials than oxides has a higher relative resistivity change than thatusing the oxide intermediate layer. This is probably because when anoxide intermediate layer is used, the interface energy is high betweenthe magnetic layers, thus causing the magnetic layers to incur a defectwhich deteriorates the characteristics.

The ferromagnetic tunneling element using the C-alloy intermediate layerhas a low relative resistivity change when produced at 300° C. or above.The reason for this is probably that the C-alloy is diffused into themagnetic layers due to heat and thus does not serve as the intermediatelayer. On the contrary, the ferromagnetic tunneling element using acompound intermediate layer exhibits a high relative resistivity changeeven when produced at 300° C. or 400° C. This is probably because thecompound intermediate layer has a high melting point; for example, themelting point of GaAs is 1238° C., the structure thus being stableagainst heating. Therefore, when a heating process is included in theproduction of the ferromagnetic tunneling element, the intermediatelayer of the ferromagnetic tunneling element should be made of acompound.

As described in detail above, the third feature of this invention isthat since the intermediate layer is made of one or more substancesselected from carbides, borides, nitrides, phosphides and group IIIb toVb elements, the soft magnetic characteristics of the magnetic layersare not deteriorated, and that the ferromagnetic tunneling elementcharacteristics are not deteriorated even if the element is passedthrough the head production heating process. This is because theintermediate layer of a compound material has a low interface energybetween the magnetic layers, thus preventing a defect from occurring inthe magnetic layers, and because the intermediate layer of a compoundmaterial has a high melting point so that the elements in theintermediate layer are not diffused into the magnetic layers even whenthe tunneling element is passed through the heating process for magnetichead production.

FIGS. 20A to 20E show the structure of an eighth embodiment of amagnetoresistance effect element of the invention. The process forproducing this embodiment will be described below.

As shown in FIG. 20A, a Cu film 61 of 10-μm width and 100-nm thicknessis formed on a glass base (not shown). Then, as shown in FIG. 20B thecentral portion thereof is worked to have grooves by ion milling, andelectrodes 62, 63, 64 and 65 are formed. The width of the grooves is 2μm. The grooves are filled with an insulating material such as a resist,and then as shown in FIG. 20C a resist 66 of 2 μm×10 μm×300 μm height isformed by photolithography. Thereafter, as shown in FIG. 20D, a 3-nmthick Fe layer 67 and a 1-nm Cr layer 68 are alternately formed toproduce a multilayered magnetic film by ion beam sputtering. Then, theupper surface of the whole element is flattened and the multilayeredmagnetic film is worked.

The above ion beam sputtering is performed under the followingconditions:

Ion gas Ar Ar gas pressure within the 2.5 × 10⁻² Pa apparatus Ion gunacceleration voltage 400 V for evaporation Ion gun ion current for 60 mAevaporation Distance between target and 127 mm substrates

The whole thickness of the Fe/Cr multilayered magnetic film is about 200nm. Moreover, the Fe/Cr multilayered magnetic film is 4 μm wide and 10μm long. Furthermore, as shown in FIG. 20E, a 500-nm thick conductivelayer 69 of Cu is formed thereon, and the multilayered magnetic filmsinsulated by the resist 66 are electrically connected to complete amagnetoresistance effect element 70.

In addition, for comparison, a magnetoresistance effect element 75 usinga conventional magnetoresistance effect multilayer is produced as shownin FIG. 21. The process for producing this magnetoresistance effectelement is as follows. A 3-nm thick Fe layer 72 and a 1-nm thick Crlayer 73 are alternately formed to produce a conventional multilayer of10 μm×10 μm×200 μm. Moreover, a lower Cu electrode 71 of 10-μm width and100-nm thickness and an upper Cu electrode 74 of 10-μm width and 100-nmthickness are provided as shown to produce a magnetoresistance effectelement 75.

The resistance of the magnetoresistance effect element 70 of thisembodiment and the magnetoresistance effect element 75 including theconventional magnetoresistance effect multilayer described above weremeasured. For the measurement, the electrodes 62, 63, 64, 65 and lowerand upper electrodes 71, 74 were selected as voltage and currentterminals, and the 4-terminal method was used. As a result, theresistance of the magnetoresistance effect element 75 for comparison was2.0×10⁻⁴ Ω, and the resistance of the magnetoresistance effect element70 of this invention was 3.5×10⁻² Ω.

Also, measurement was made of the amount of resistivity change of themagnetoresistance effect element 70 of the embodiment and themagnetoresistance effect element 75 for comparison with respect to thechange of the applied magnetic field. The measurement was made at roomtemperature. FIG. 22 shows the measured result. From FIG. 22, it will beseen that the amount of resistivity change 76 of the magnetoresistanceeffect element 70 of this embodiment is about 5 times the amount ofresistivity change 77 of the magnetoresistance effect element 75 forcomparison.

As described above, since the element using the Fe/Cr multilayered filmsis constructed so that electrons are passed a plurality of times throughthe nonmagnetic layer located at the same distance from the substrate,the electrical resistance of the whole element can be increased andgreatly changed without increasing the thickness of the whole element.Since the thickness of the whole element is not changed, the resolutionis not reduced relative to the magnetic field distribution in thewavelength direction when the element is used in a magnetic head.

FIG. 23 shows the structure of a ninth embodiment of a magnetoresistanceeffect element of this invention. This element has the same structure asthe eighth embodiment, and uses the ferromagnetic tunneling effect. Themagnetic layers are an Fe-1.7 at % Ru alloy layer 85 of 100-nm thicknessand an Fe-2.0 at % C alloy layer 84 of 100-nm thickness. The nonmagneticlayer 86 is made of 10-nm thick Al₂O₃. The electrode 81 and theconductive layer 87 are made of Cu. Resists 82 and 83 are used asinsulating materials.

A magnetic field from a Helmholtz coil was applied to themagnetoresistance effect element, and the change of electricalresistance was examined. As a result, it was found that the electricalresistance of the element changes with the change of the magnitude ofthe magnetic field.

The causes of the resistivity change are considered as follows.

By the measurement of the magnetization curves, it was found that thecoercive force of the Fe-1.7 at % Ru alloy layer is 25 Oe, and that thecoercive force of the Fe-2.0 at % C alloy layer is 8 Oe. When themagnitude of the magnetic field is changed, the magnetization directionof the Fe-2.0 at % C alloy layer is changed at 8 Oe, but themagnetization direction of the Fe-1.7 at % Ru alloy layer is notchanged. When a magnetic field of 25 Oe or above is applied, themagnetization direction of the Fe-1.7 at % Ru alloy layer is changed.Therefore, in a magnetic field of ±8 to 25 Oe, the magnetizationdirection of the Fe-2.0 at % C alloy layer and the magnetizationdirection of the Fe-1.7 at % Ru alloy layer are antiparallel. Also,outside of this range of magnetic field, the magnetization directionsare parallel. When a tunneling current is flowed in the Al₂O₃ layer, theconductance is higher when the magnetization directions are parallelthan when they are antiparallel. Thus, the electrical resistance of theelement is changed with the magnitude of the magnetic field.

Moreover, when the electrical resistivity change of themagnetoresistance effect element of the structure in which electrons arepassed once through the Al₂O₃ was measured, the amount of resistivitychange was ½ that of the magnetoresistance effect element of thisinvention. As described above, if the element is constructed so thatelectrons are passed a plurality of times through the nonmagnetic layerlocated at the same distance from the substrate, the electricalresistance of the whole element can be increased and a large amount ofresistivity change can be achieved without increasing the thickness ofthe whole element. Since the thickness of the whole element is notchanged, the resolution is not reduced relative to the magnetic fielddistribution in the wavelength direction when the element is used in amagnetic head.

FIG. 24 shows the cross-sectional structure of a tenth embodiment of amagnetoresistance element of the invention. This element uses theferromagnetic spin-dependent tunneling effect. The Corning-photoceramwas used as a substrate 91. An insulator 92 was made of a resin. Theconducting layers 93, 94 were made of Cu. The magnetic layers were a100-nm thick Fe-2.0 at % C alloy layer 95 and a 100-nm thick Fe-1.7 at %Ru alloy layer 96. The nonmagnetic layer was a 10-nm thick Al₂O₃ layer97.

As shown in FIG. 24, the magnetoresistance effect element of thisembodiment has a plurality of ferromagnetic tunneling elements connectedin series. Thus, the electrical resistance of the whole element becomeslarge, and the amount of resistivity change is large, so that theelement is able to act as a high-sensitivity magnetic field sensor.

The series connection of the ferromagnetic tunneling elements may bemade in any shape, but as the element is large, the resolution relativeto the magnetic field distribution is decreased so that the element isnot suitable for the magnetic head. However, the magnetic sensor whichdoes not require the resolution relative to the magnetic fielddistribution is preferably formed with a magnetoresistance effectelement having a great number of ferromagnetic tunneling elementsconnected in series as in this embodiment.

As described in detail, the fourth feature of the invention is that inthe element having the Fe/Cr multilayered films and the element havingthe magnetoresistance effect due to the multilayered structure such asthe ferromagnetic tunneling element, the electrical resistance and theamount of resistivity change of the whole element can be increased byseries connection of a plurality of magnetoresistance effect elements.Moreover, when the element is so constructed that electrons are passed aplurality of times through the nonmagnetic layer located at the samedistance from the substrate, the electrical resistance and the amount ofresistivity change of the whole element can be increased withoutincreasing the thickness of the whole element. Since the thickness ofthe whole element is not changed, the resolution is not decreasedrelative to the magnetic field distribution in the wavelength directionwhen the element is used in a magnetic head.

Before the magnetic head of this invention is described, the principleof the magnetism detection will be described with reference to FIGS.25A, 25B and 26. A magnetic sensing element is used which hasferromagnetic layers 1010 a and 101 b connected in series through anelectrically insulating film 102 as shown in FIGS. 25A and 25B. Thethickness of the electrically insulating film 102 is in such a rangefrom 0.5 nm to 10 nm that the tunneling current can be flowed in thefilm, preferably in a range from 1 nm to 6 nm. An electric circuit asshown in FIGS. 25A and 25B is connected to this multilayered element,and the current flowing through the circuit is measured. When thiselement is placed in the magnetic field leaked from a magnetic recordingmedium 103, a part of the ferromagnetic metal layers 101 a and 101 bwhich is made to contact with the electrically insulating film 102 isaffected and magnetized by the leaked magnetic field. Under thiscondition, the tunneling current which reflects the electron state ofthe part of the ferromagnetic metal 101 a, 101 b in contact with theelectrically insulating film 102 is flowed in the element. Under thiselectron state, the element is delicately affected not only by thetemperature and crystalline property of the ferromagnetic metal but alsoby the magnetization state such as the magnetization direction and thepresence of the magnetic wall.

When this element is placed, as shown in FIG. 25B, in a magnetic fieldopposite to that shown in FIG. 25A, the magnetization state of theferromagnetic metal 101 a, 101 b is changed from the case of FIG. 25A.As a result, the electron state of the part of the ferromagnetic metal101 a, 101 b in contact with the electrically insulating film 102 ischanged, and the tunnel current is changed. That is, each time themultilayered element passes by the recorded bits periodically recordedon the magnetic recording medium, the current is changed in accordancewith the magnetization direction of the recorded bits. FIG. 26 shows thechange of the current. In FIGS. 25A and 25B, reference numeral 104represents the base on which a magnetic recording medium 103 is formed.

The two ferromagnetic metal layers 101 a, 101 b stacked about theelectrically insulating film 102 may be made of the same material, butin order to greatly change the current according to the change ofmagnetic field, the two metal layers are desired to be made of differentmaterials having different work functions. The value of the tunnelingcurrent is affected not only by the thickness of the electricallyinsulating film 102 but also by the difference between the workfunctions of the ferromagnetic metal layers 101 a and 101 b. The workfunction difference is above 0.3 eV, preferably above 0.5 eV for theobservation of a large current change.

Although the ferromagnetic layers 101 a, 101 b may be of crystallineproperty or noncrystalline property, in order to have a high-speedresponse to the direction change of the magnetic field leaking from themagnetic recording medium 103 it is desired that they be made of a softmagnetic material excellent in the high-frequency characteristic. Thesoft magnetic material may be Fe-, Co- or Ni-based material such as Fe,Fe—Ni, Co—Nb—Zr, Co—Nb—Ta, Fe—Si, Ni—Fe—B.

For measurement of the tunneling current, the electrically insulatingfilm 102 shown in FIGS. 25A and 25B is not limited to a good insulatingmaterial such as Al₂O₃ or SiO₂, but may be a semiconductor or semimetalsuch as Si, B or GaAs. The specific resistance difference to theferromagnetic metal 101 a, 101 b should be great.

While the electrically insulating film 102 for explaining the principleof the invention is single as shown in FIGS. 25A and 25B, a plurality ofcombinations of the ferromagnetic metal 101 a, 101 b and theelectrically insulating film 102 may be provided from the principlepoint of view, and a magnetic artificial lattice can be effectivelyused.

An embodiment of the magnetic head of the invention will be describedbelow.

FIGS. 27A and 27B show the structure of a first embodiment of themagnetic head. This magnetic head is a thin film-type ring head, and thecross-sectional structure is shown in FIG. 27A. A substrate 105 of thisthin-film type ring head is made of Mn—Zn ferrite material, and a lowermagnetic pole 106 and an upper magnetic pole 107 are made of Permalloymaterial and are 20 μand 15 μm thick, respectively. The material in thegap 108 is Al₂O₃, the gap distance is 0.5 μm, and the coil 109 is madeof Cu.

On the thin-film type ring head is formed an electrically insulatingfilm 110 which is made of Al₂O₃ and of which the thinnest part has athickness of 3 nm. On this insulating film is formed a 15-μmferromagnetic material 111 which is made of Fe—Si—Al.

FIG. 27B shows the magnetic head produced by the above process. Thismagnetic head uses its thin-film ring head as a recording element. Theferromagnetic material 111 formed thereon through the electricallyinsulating film 110 and the upper magnetic pole 107 of the thin-filmring head are paired to form a reproducing element for the dual-elementmagnetic head. This magnetic head uses the upper magnetic pole of thethin-film ring head as part of the element structure for recording andreproducing, and thus the whole construction of the magnetic head can besimplified.

The ferromagnetic material of the top layer as shown in FIG. 27B isselected to be Permalloy (Fe—Ni), Fe, Fe—Si, Ni, Ni—Fe—B, Co, Co—Nb—Zr,Co—Ta—Zr, and the other portions of the magnetic head are the same asdescribed above.

The characteristics of the magnetic head are evaluated under thefollowing conditions. The magnetic recording medium used is a 5-inchdiameter rigid magnetic disk. The magnetic films are a Co—Ni-basedmedium (having a surface direction coercive force of 900 Oe and asaturated magnetization of 600 emu/cc) as an in-plane magnetized filmand a Co—Cr-based medium (having a vertical direction coercive force 700Oe and a saturated magnetization of 520 emu/cc) as a perpendicularmagnetized film. The spacing between the head and the medium is selectedto be 0.15 μm, and the relative moving speed is 15 m/s. The recordingdensity is selected to be 1 kFCI and 50 kFCI, and the thin-film ringhead is used for recording.

The signal/noise ratio (S/N) of the reading output is measured. Forcomparison, the thin-film ring head for recording is used for readingand the S/N ratio is measured and used. Tables 2 and 3 list the measuredresults of the Co—Ni-based in-plane magnetized film and Co—Cr-basedperpendicular magnetization film, respectively. In the tables, thedifference between the work functions is of the Permalloy of theferromagnetic material 111 and the upper magnetic pole 107.

TABLE 2 Recording medium: Co—Ni-based surface magnetized filmFerromagentic materials and work function difference (eV) Ring headRecording (for density reference) Permalloy Fe—Si—Al Fe—Si Fe Ni Ni—Fe—BCo Co—Nb—Zr Co—Ta-Z — 0 0.55 0.3 0.2 0.1 0.6 1.2 0.9 0.85  1 kFCI 1 2.65.3 4.0 3.2 2.2 4.6 2.0 9.4 8.6 50 kFCI 0.8 2.2 5.0 3.9 2.6 1.7 4.1 1.69.0 7.8

TABLE 3 Recording medium: Co—Cr-based perpendicular magnetized filmFerromagentic materials and work function difference (eV) Ring headRecording (for density reference) Permalloy Fe—Si—Al Fe—Si Fe Ni Ni—Fe—BCo Co—Nb—Zr Co—Ta-Z — 0 0.55 0.3 0.2 0.1 0.6 1.2 0.9 0.85  1 kFCI 1 2.15.0 3.9 3.0 2.0 4.4 1.6 6.8 8.1 50 kFCI 0.9 1.6 4.6 3.4 2.1 1.3 4.0 1.15.2 6.9

FIGS. 28A, 28B and 28C show the structure of a second embodiment of themagnetic head. The substrate 121 is made of sapphire. The Fe film of aferromagnetic material 122 is first deposited to a thickness of 20 μm bysputtering (FIG. 28A), and a 2-nm thick semiconductor 123 of Si and a10-nm ferromagnetic material 124 of Fe—C are alternately formed, for atotal of three layers are formed in turn (FIG. 28B). Then, a lowermagnetic pole 125 of Permalloy, a gap 127 of Al₂O₃, a coil 128 of Cu andan upper magnetic pole 126 of Co—Nb—Zr are provided thereon in turn bythe normally used thin-film manufacturing technology. FIG. 28C shows themagnetic head produced by the above process.

The magnetic head of this embodiment, of which the electricallyinsulating film to be interposed between the ferromagnetic materials ischanged to a semiconductor, was evaluated under the same conditions asin the first embodiment. The result was that even in any case of theCo—Ni-based in-plane magnetized film and the Co—Cr-based perpendicularmagnetization film, when the medium recorded at a linear recordingdensity of 1 kFCI, 50 kFCI was reproduced, the S/N ratio was at least 3times larger than the S/N ratio reproduced by the conventional ringhead.

A third embodiment of the magnetic head will be described below.

The electrically insulating material 110 of the magnetic head is made ofSiO₂, MnO, NiO, BeO, SiO₂—Al₂O₃, Mn—Zn ferrite, Y₂O₃, ZrO₂, TiO₂ inplace of Al₂O₃ in the first embodiment. The Mn—Zn ferrite is aferromagnetic material but an electrically insulating material which canbe used as an electrically insulating film as the other oxides are usedas electrically insulating materials.

A fourth embodiment of the magnetic head will be mentioned.

The electrically insulating film 110 in the first embodiment is made ofSi, B, BN in place of Al₂O₃.

The characteristics of the magnetic heads produced in the third andfourth embodiments are evaluated under the same conditions as in thefirst embodiment. The change of the current flowing between theferromagnetic material 111 (FIG. 27B) and the upper magnetic pole ismeasured. The S/N ratio of either magnetic head is at least twice theS/N ratio of the thin-film ring head.

Thus, the fifth feature of this invention is that when the magneticallyrecorded information is reproduced, the S/N ratio is much greater thanthat of the reproduced signal by the conventional ring head. Theconstruction is simple, and the reproducing element of this embodimentcan be easily provided to be overlapped on the recording element. Thus,the dual-element magnetic head for both recording and reproducing can beproduced by a simple process. Since the S/N ratio upon reproduction canbe greatly improved by use of the magnetic head according to thisembodiment, the high-density magnetically recorded medium can bereproduced even when the spacing between the magnetic head and therecording medium is slightly large. Thus, the probability of an accidentsuch as head crush can be reduced. When this magnetic head is used inmagnetic disk apparatus, the reliability of the apparatus and themagnetic writing and reading characteristics of the apparatus forhigh-density recorded regions can be greatly improved.

1. A magnetic apparatus, comprising: a perpendicular magnetic recordingmedium; and a magnetic head including a reproducing element arranged toperform reproduction from the perpendicular magnetic recording medium,wherein said reproducing element has a magnetic-resistance elementincluding a first non-magnetic metal layer, a second non-magnetic metallayer, and a magneto-resistance effect film formed between the firstnon-magnetic metal layer and the second non-magnetic metal layer, saidmagneto-resistance effect film includes a first ferromagnetic layer, asecond ferromagnetic layer, an intermediate insulating layer formedbetween the first ferromagnetic layer and the second ferromagneticlayer, and an anti-ferromagnetic layer formed between the secondferromagnetic layer and the second non-magnetic metal layer, and saidmagneto-resistance effect film is arranged so that a tunnel currentflows between the first ferromagnetic layer and the second ferromagneticlayer through the intermediate insulating layer.
 2. A magnetic apparatusaccording to claim 1, wherein a magnetization direction of said firstferromagnetic layer changes in the presence of a changing externalmagnetic field.
 3. A magnetic apparatus according to claim 1, whereinsaid perpendicular magnetic recording medium has a perpendicularmagnetic recording layer comprising Co—Cr.
 4. A magnetic apparatusaccording to claim 1, wherein a magnetization direction of said secondferromagnetic layer is fixed by the anti-ferromagnetic layer whichapplies a bias magnetic field to the second ferromagnetic layer.
 5. In amagnetic apparatus of the type having a perpendicular magnetic recordingmedium and a magnetic bead arranged to perform reproduction from theperpendicular magnetic recording medium, the improvement wherein: themagnetic head includes a reproducing element, wherein said reproducingelement has a magnetic-resistance element including a first non-magneticmetal layer, a second non-magnetic metal layer, and a magneto-resistanceeffect film formed between the first non-magnetic metal layer and thesecond non-magnetic metal layer, said magneto-resistance effect filmincludes a first ferromagnetic layer, a second ferromagnetic layer, anintermediate insulating layer formed between the first ferromagneticlayer and the second ferromagnetic layer, and an anti-ferromagneticlayer formed between the second ferromagnetic layer and the secondnonmagnetic metal layer, and said magneto-resistance effect film isarranged so that a tunnel current flows between the first ferromagneticlayer and the second ferromagnetic layer through the intermediateinsulating layer.
 6. A magnetic apparatus according to claim 5, whereina magnetization direction of said first ferromagnetic layer changes inthe presence of a changing external magnetic field.
 7. A magneticapparatus according to claim 5, wherein a magnetization direction ofsaid second ferromagnetic layer is fixed by the anti-ferromagnetic layerwhich applies a bias magnetic field to the second ferromagnetic layer.